EP0150456A2 - Vieillissement à température relativement basse d'un alliage d'aluminium, contenant du lithium - Google Patents
Vieillissement à température relativement basse d'un alliage d'aluminium, contenant du lithium Download PDFInfo
- Publication number
- EP0150456A2 EP0150456A2 EP84115925A EP84115925A EP0150456A2 EP 0150456 A2 EP0150456 A2 EP 0150456A2 EP 84115925 A EP84115925 A EP 84115925A EP 84115925 A EP84115925 A EP 84115925A EP 0150456 A2 EP0150456 A2 EP 0150456A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- aluminum
- lithium
- percent
- aged
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
Definitions
- the present invention relates to aluminum alloys, more particularly to aluminum alloys containing lithium as an alloying element, and most particularly to a process for improving the fracture toughness of aluminum-lithium alloys without detracting from their strength.
- aluminum-lithium alloys have been used only sparsely in aircraft structure.
- the relatively low use has been caused by casting difficulties associated with aluminum-lithium alloys and by their relatively low fracture toughness compared to other more conventional aluminum alloys.
- Aluminum-lithium alloys provide a substantial lowering of the density of aluminum alloys (as well as a relatively high strength to weight ratio), which has been found to be very important in decreasing the overall weight of structural materials used in an aircraft. While substantial strides have been made in improving the aluminum-lithium processing technology, a major challenge is still to obtain a good blend of fracture toughness and high strength with an aluminum-lithium alloy.
- the present invention provides a method for aging aluminum-lithium alloys of various composition at relatively low temperatures to develop a high fracture toughness without reducing the strength of the alloy to any significant extent.
- the alloy is aged at a relatively low temperature for a relatively long time. This process may be generally referred to as low temperature underaging. More specifically, the alloy can be aged at temperatures ranging from 200° F to 300° F for a period of time ranging from 1 up to 70 or more hours.
- This low temperature aging regimen will result in an alloy having a strength level generally equivalent to or only slightly lower than that of peak aged material while maintaining a fracture toughness on the order of 150 to 200 percent greater than that of materials aged at conventional higher temperatures.
- An aluminum-lithium alloy formulated in accordance with the present invention can contain from about 1.0 to about 3.2 percent lithium.
- the current data indicates that the benefits of the low temperature aging are most apparent at lithium levels of 2.7 percent and below. All percentages herein are by weight percent based on the total weight of the alloy unless otherwise indicated.
- Additional alloying agents such as magnesium and copper can also be included in the alloy.
- the magnesium in the alloy functions to increase strength and slightly decrease density. It also provides solid solution strengthening.
- the copper adds strength to alloy, but unfortunately also serves to increase density.
- Grain refiners such as zirconium can also be also be included.
- Manganese can also be present alone or together with zirconium. The manganese functions to provide an improved combination of strength and fracture toughness.
- Iron and silicon can each be present in amounts up to 0.3 percent. It is preferred, however, that these elements be present only in trace amounts of less than 0.10 percent. Certain trace elements such as zinc may be present in amounts up to but not to exceed 0.25 percent. Certain other trace elements such as chromium must be held to levels of 0.05 percent or less. If these maximums are exceeded, the desired properties of the aluminum-lithium alloy will tend to deteriorate.
- the trace elements sodium and hydrogen are also thought to be harmful to the properties (fracture toughness in particular) of aluminum-lithium alloys and should be held to the lowest levels practically attainable, for example on the order of 15 to 30 ppm (0.0015-0.0030 wt. %) for the sodium and less than 15 ppm (0.0015 wt. %) and preferably less than 1.0 ppm (0.0001 wt. %) for the hydrogen.
- the balance of the alloy comprises aluminum.
- the following table represents the proportions in which the alloying and trace elements may be present.
- the broadest ranges are acceptable under most circumstances, while the preferred ranges provide a better balance of fracture toughness, strength and corrosion resistance.
- the most preferred ranges yield alloys that presently provide the best set of overall properties for use in aircraft structure.
- a most preferred alloy that is especially susceptible to property enhancement in accordance with the techniques of the present invention is an alloy containing 2.2 to 2.8 percent lithium, 0.4 to 0.8 percent magnesium, 1.5 to 2.1 percent copper and up to 0.15 percent zirconium as a grain refiner.
- the preferred limitations on iron, silicon and other trace elements also applies to this preferred alloy.
- An aluminum-lithium alloy formulated in the proportions set forth in the foregoing paragraphs is processed into an article utilizing known techniques.
- the alloy is formulated in molten form and cast into an ingot.
- the ingot is then homogenized at temperatures ranging from 925 F to 1000° F.
- the alloy is converted into a usable article by conventional mechanical formation techniques such as rolling, extrusion or the like.
- the alloy is normally subjected to a solution treatment at temperatures ranging from 950° F to 1000° F, quenched in a quenching medium such as water that is maintained at a temperature on the order of 70° F to 150° F. If the alloy has been rolled or extruded, it is generally stretched on the order of 1 to 3 percent of its original length to relieve internal stresses.
- the aluminum alloy can then be further worked and formed into the various shapes for its final application. Additional heat treatments such as solution heat treatment can be employed if desired. For example, an extruded product after being cut to desired length are generally solution heat treated at temperatures on the order of 975° F for 1 to 4 hours. The product is then quenched in a quenching medium held at temperatures ranging from about 70 0 F to 150° F.
- the article is subjected to an aging treatment that will increase the strength of the material, while maintaining its fracture toughness and other engineering properties at relatively high levels.
- the articles are subjected to a low temperature underage heat treatment at temperatures ranging from about 200 0 F to about 300° F. It is preferred that the alloy be heat treated in the range of from about 250° F to 275° F. At the higher temperatures, less time is needed to bring about the proper balance between strength and fracture toughness than at lower aging temperatures, but the overall property mix will be slightly less desirable.
- the aging when the aging is conducted at temperatures on the order of 275° F to 300° F, it is preferred that the product be subjected to the aging temperature for periods of from 1 to 40 hours. On the other hand, when aging is conducted at temperatures on the order of 250° F or below, aging times from 2 to 80 hours or more are preferred to bring about the proper balance between fracture toughness and strength. After the aging treatment, the aluminum-lithium articles are cooled to room temperature.
- the treatment will result in an aluminum-lithium alloy having an ultimate strength on the order of 65 to 95 ksi, depending on the detail composition of the alloy.
- the fracture toughness of the material will be on the order of 1 1/2 to 2 times greater than that of similar aluminum-lithium alloys subjected to conventional aging treatments, which are normally conducted at temperatures greater than 300° F .
- the superior strength and toughness combination achieved by the low temperature underaging techniques in accordance with the present invention also surprisingly causes some aluminum-lithium alloys to exhibit an improvement in stress corrosion resistance when contrasted with the same alloy aged by standard aging practices. Examples of these improved characteristics will be set forth in more detail in conjunction with the ensuing examples.
- An aluminum alloy containing 2.4 lithium, 1 percent magnesium, 1.3 percent copper, 0.15 percent zirconium with the balance being aluminum was formulated.
- the trace elements present in the formulation constituted less than 0.25 percent of the total.
- the iron and silicon present in the formulation constituted less than 0.07 percent each of the formulation.
- the alloy was cast and homogenized at 975° F. Thereafter, the alloy was hot rolled to a thickness of 0.2 inches. The resulting sheet was then solution treated at 975° F for about 1 hour. It was then quenched in water maintained at about 70° F. Thereafter, the sheet was subjected to a stretch of 1 1/2 percent of its initial length and then material was then cut into specimens.
- the specimens were cut to a size of 0.5 inch by 2 1/2 inch by 0.2 inch for the precrack Charpy impact tests, a known method of measuring fracture toughness.
- the specimens prepared for the tensile strength tests were 1 inch by 4 inches by 0.2 inches.
- a plurality of specimens were then aged at 350° F for 4, 8 and 16 hours; at 325° F for 8, 16, and 48 hours; at 305° F for 8 hours; at 275OF for 16 and 40 hours; and at 250° F for 40 and 72 hours.
- Each of the specimens aged at each of the temperatures and times were then subjected to the tensile strength and precrack Charpy impact tests in accordance with standard testing procedures.
- the values of each of the specimens aged at a particular time and temperatures were then averaged. These average values are set forth in the graph of FIGURE 1.
- FIGURE 1 By observing FIGURE 1 it will be readily observed that specimens aged at temperatures greater than 300° F exhibit a toughness on the order of from 225 to 525 inch-pounds per square inch as measured by the Charpy impact test. By contrast, the specimens underaged at a low temperature in accordance with the present invention exhibit toughnesses on the order of 650 to almost 850- inch pounds per square inch as indicated by the Charpy impact test. At the same time, the average strength of the materials fall generally within the 64 to 71 ksi range, with the exception of the specimens aged at 350° F for 16 hours. These specimens, however, exhibited the lowest toughness of any of the specimens.
- An aluminum alloy containing from 2 percent lithium, 1 percent magnesium, 2.5 percent copper, 0.15 percent zirconium, and the balance aluminum was formulated.
- the trace elements totaled less than 0.25 percent of the total composition, while the iron and silicon were maintained at less than 0.07 percent of the total formulation.
- the alloy was cast and homogenized at a temperature of about 975° F.
- the alloy was then extruded into a bar having cross-sectional dimensions of 0.75 inch by 2.5 inch.
- the bar was then cut into predetermined lengths and solution heat treated at about 975° F for 1 hour. Thereafter, the articles were quenched in either 70° F or 180 0 F water. Once the bars had cooled, they were stretched approximately 1 1/2 percent of their original length.
- the bars were then fabricated into double cantilever bean (DCB) test specimens for measuring crack growth velocity during stress corrosion cracking. These specimens have a length of approximately six (6) inches.
- DCB double cantilever bean
Landscapes
- Chemical & Material Sciences (AREA)
- Mechanical Engineering (AREA)
- Organic Chemistry (AREA)
- Metallurgy (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Forging (AREA)
- Heat Treatment Of Steel (AREA)
- Conductive Materials (AREA)
- Secondary Cells (AREA)
- Battery Electrode And Active Subsutance (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US56722783A | 1983-12-30 | 1983-12-30 | |
US567227 | 1983-12-30 |
Publications (3)
Publication Number | Publication Date |
---|---|
EP0150456A2 true EP0150456A2 (fr) | 1985-08-07 |
EP0150456A3 EP0150456A3 (en) | 1986-10-08 |
EP0150456B1 EP0150456B1 (fr) | 1990-11-14 |
Family
ID=24266272
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP84115925A Expired - Lifetime EP0150456B1 (fr) | 1983-12-30 | 1984-12-20 | Vieillissement à température relativement basse d'un alliage d'aluminium, contenant du lithium |
Country Status (4)
Country | Link |
---|---|
US (1) | US4840682A (fr) |
EP (1) | EP0150456B1 (fr) |
JP (1) | JPH0660371B2 (fr) |
DE (1) | DE3483607D1 (fr) |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0227563A1 (fr) * | 1985-11-28 | 1987-07-01 | Cegedur Pechiney Rhenalu | Procédé de désensibilisation à la corrosion exfoliante avec obtention simultanée d'une haute résistance mécanique et bonne tenue aux dommages des alliages d'aluminium contenant du lithium |
US4861391A (en) * | 1987-12-14 | 1989-08-29 | Aluminum Company Of America | Aluminum alloy two-step aging method and article |
US4869870A (en) * | 1988-03-24 | 1989-09-26 | Aluminum Company Of America | Aluminum-lithium alloys with hafnium |
US4961792A (en) * | 1984-12-24 | 1990-10-09 | Aluminum Company Of America | Aluminum-lithium alloys having improved corrosion resistance containing Mg and Zn |
US5066342A (en) * | 1988-01-28 | 1991-11-19 | Aluminum Company Of America | Aluminum-lithium alloys and method of making the same |
US5085830A (en) * | 1989-03-24 | 1992-02-04 | Comalco Aluminum Limited | Process for making aluminum-lithium alloys of high toughness |
US5108519A (en) * | 1988-01-28 | 1992-04-28 | Aluminum Company Of America | Aluminum-lithium alloys suitable for forgings |
US5137686A (en) * | 1988-01-28 | 1992-08-11 | Aluminum Company Of America | Aluminum-lithium alloys |
US5422066A (en) * | 1989-03-24 | 1995-06-06 | Comalco Aluminium Limited | Aluminum-lithium, aluminum-magnesium and magnesium-lithium alloys of high toughness |
Families Citing this family (17)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4999061A (en) * | 1983-12-30 | 1991-03-12 | The Boeing Company | Low temperature underaging of lithium bearing alloys and method thereof |
EP0151301B1 (fr) * | 1983-12-30 | 1989-06-07 | The Boeing Company | Alliage aluminium-lithium |
CA1337747C (fr) * | 1986-12-01 | 1995-12-19 | K. Sharvan Kumar | Alliages ternaires aluminium-lithium |
JPH0814018B2 (ja) * | 1987-12-14 | 1996-02-14 | アルミニウム カンパニー オブ アメリカ | アルミニウム合金の熱処理方法 |
US5462712A (en) * | 1988-08-18 | 1995-10-31 | Martin Marietta Corporation | High strength Al-Cu-Li-Zn-Mg alloys |
US5455003A (en) * | 1988-08-18 | 1995-10-03 | Martin Marietta Corporation | Al-Cu-Li alloys with improved cryogenic fracture toughness |
US5512241A (en) * | 1988-08-18 | 1996-04-30 | Martin Marietta Corporation | Al-Cu-Li weld filler alloy, process for the preparation thereof and process for welding therewith |
US5211910A (en) * | 1990-01-26 | 1993-05-18 | Martin Marietta Corporation | Ultra high strength aluminum-base alloys |
US5133931A (en) * | 1990-08-28 | 1992-07-28 | Reynolds Metals Company | Lithium aluminum alloy system |
US5198045A (en) * | 1991-05-14 | 1993-03-30 | Reynolds Metals Company | Low density high strength al-li alloy |
ES2445745T3 (es) | 1997-09-22 | 2014-03-05 | Eads Deutschland Gmbh | Aleación sobre una base de aluminio y procedimiento para su tratamiento térmico |
US7056395B1 (en) * | 1999-09-01 | 2006-06-06 | Brush Wellman, Inc. | Dies for die casting aluminum and other metals |
US6368427B1 (en) * | 1999-09-10 | 2002-04-09 | Geoffrey K. Sigworth | Method for grain refinement of high strength aluminum casting alloys |
US7105067B2 (en) * | 2003-06-05 | 2006-09-12 | The Boeing Company | Method to increase the toughness of aluminum-lithium alloys at cryogenic temperatures |
BRPI0820679A2 (pt) | 2007-12-04 | 2019-09-10 | Alcoa Inc | ligas alumínio-cobre-lítio melhoradas |
US8333853B2 (en) * | 2009-01-16 | 2012-12-18 | Alcoa Inc. | Aging of aluminum alloys for improved combination of fatigue performance and strength |
CN112646994B (zh) * | 2020-12-16 | 2022-03-04 | 中南大学 | 一种高比强高比模铝合金及其制备方法 |
Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB787665A (en) * | 1955-04-05 | 1957-12-11 | Stone & Company Charlton Ltd J | Improvements relating to aluminium-base alloys |
US2915391A (en) * | 1958-01-13 | 1959-12-01 | Aluminum Co Of America | Aluminum base alloy |
GB2115836A (en) * | 1982-02-26 | 1983-09-14 | Secr Defence | Improvements in or relating to aluminium alloys |
EP0090583A2 (fr) * | 1982-03-31 | 1983-10-05 | Alcan International Limited | Traitement thermique d'alliages d'aluminium |
EP0124286A1 (fr) * | 1983-03-31 | 1984-11-07 | Alcan International Limited | Alliages d'aluminium |
Family Cites Families (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS602644A (ja) * | 1983-03-31 | 1985-01-08 | アルカン・インタ−ナシヨナル・リミテイド | アルミニウム合金 |
-
1984
- 1984-12-20 EP EP84115925A patent/EP0150456B1/fr not_active Expired - Lifetime
- 1984-12-20 DE DE8484115925T patent/DE3483607D1/de not_active Expired - Lifetime
- 1984-12-28 JP JP59282086A patent/JPH0660371B2/ja not_active Expired - Lifetime
-
1985
- 1985-11-21 US US06/800,503 patent/US4840682A/en not_active Expired - Lifetime
Patent Citations (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB787665A (en) * | 1955-04-05 | 1957-12-11 | Stone & Company Charlton Ltd J | Improvements relating to aluminium-base alloys |
US2915391A (en) * | 1958-01-13 | 1959-12-01 | Aluminum Co Of America | Aluminum base alloy |
GB2115836A (en) * | 1982-02-26 | 1983-09-14 | Secr Defence | Improvements in or relating to aluminium alloys |
EP0090583A2 (fr) * | 1982-03-31 | 1983-10-05 | Alcan International Limited | Traitement thermique d'alliages d'aluminium |
EP0124286A1 (fr) * | 1983-03-31 | 1984-11-07 | Alcan International Limited | Alliages d'aluminium |
Non-Patent Citations (4)
Title |
---|
ALUMINIUM-LITHIUM ALLOYS II, CONFERENCE PROCEEDINGS OF ALUMIMIUM-LITHIUM ALLOYS II, Monterey, US, 12th-14th April 1983, pages 363-391, AIME, Warrendale, US; PEEL et al.: "The development and application of improved alumimium-lithium alloys" * |
ALUMINIUM-LITHIUM ALLOYS II, CONFERENCE PROCEEDINGS OF ALUMINIUM-LITHIUM ALLOYS II, Monterey, US, 12th-14th April 1983, pages 219-233, AIME, Warrendale, US; HARRIS et al.: "Effect of composition and heat treatment on strength and fracture characteristics of Al-Li-Mg alloys * |
ALUMINIUM-LITHIUM ALLOYS II, CONFERENCE PROCEEDINGS OF ALUMINIUM-LITHIUM ALLOYS II, Monterey, US, 12th-14th April 1983, pages 393-405, AIME, Warrendale, US; SANKARAN et al.: "Structure-property relationships in Al-Cu-Li alloys" * |
CHEMICAL ABSTRACTS, vol. 78, no. 20, 21st May 1973, page 217, abstract no. 127717e, Columbus, Ohio, US; A. CHERNYAK et al.: "Mechanical properties of 01420 aluminum alloy sheet after aging", & METALLOVED. TERM. OBRAB. METAL. (1973), (1), 75-6 * |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4961792A (en) * | 1984-12-24 | 1990-10-09 | Aluminum Company Of America | Aluminum-lithium alloys having improved corrosion resistance containing Mg and Zn |
EP0227563A1 (fr) * | 1985-11-28 | 1987-07-01 | Cegedur Pechiney Rhenalu | Procédé de désensibilisation à la corrosion exfoliante avec obtention simultanée d'une haute résistance mécanique et bonne tenue aux dommages des alliages d'aluminium contenant du lithium |
US4861391A (en) * | 1987-12-14 | 1989-08-29 | Aluminum Company Of America | Aluminum alloy two-step aging method and article |
US5066342A (en) * | 1988-01-28 | 1991-11-19 | Aluminum Company Of America | Aluminum-lithium alloys and method of making the same |
US5108519A (en) * | 1988-01-28 | 1992-04-28 | Aluminum Company Of America | Aluminum-lithium alloys suitable for forgings |
US5137686A (en) * | 1988-01-28 | 1992-08-11 | Aluminum Company Of America | Aluminum-lithium alloys |
US4869870A (en) * | 1988-03-24 | 1989-09-26 | Aluminum Company Of America | Aluminum-lithium alloys with hafnium |
US5085830A (en) * | 1989-03-24 | 1992-02-04 | Comalco Aluminum Limited | Process for making aluminum-lithium alloys of high toughness |
US5422066A (en) * | 1989-03-24 | 1995-06-06 | Comalco Aluminium Limited | Aluminum-lithium, aluminum-magnesium and magnesium-lithium alloys of high toughness |
Also Published As
Publication number | Publication date |
---|---|
DE3483607D1 (de) | 1990-12-20 |
EP0150456A3 (en) | 1986-10-08 |
JPS60215750A (ja) | 1985-10-29 |
JPH0660371B2 (ja) | 1994-08-10 |
US4840682A (en) | 1989-06-20 |
EP0150456B1 (fr) | 1990-11-14 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
EP0150456A2 (fr) | Vieillissement à température relativement basse d'un alliage d'aluminium, contenant du lithium | |
US4603029A (en) | Aluminum-lithium alloy | |
EP0546103B1 (fr) | Systeme d'alliage de lithium et d'aluminium ameliore | |
JP4903039B2 (ja) | 特に航空宇宙用途向けの、耐損傷性が高いアルミニウム合金製品 | |
CA1228490A (fr) | Alliages d'aluminium et lithium | |
EP1945825B1 (fr) | Alliages a base d'aluminium, de cuivre et de magnesium (al cu mg) pour les applications aerospatiales | |
EP0377779B2 (fr) | Produit en alliage d'aluminium ayant des combinaisons de résistance mécanique, de ténacité et de résistance à la corrosion modifiées | |
US4735774A (en) | Aluminum-lithium alloy (4) | |
JP4185247B2 (ja) | アルミニウム系合金及びその熱処理方法 | |
EP0156995A1 (fr) | Alliage aluminium-lithium | |
US4999061A (en) | Low temperature underaging of lithium bearing alloys and method thereof | |
US4812178A (en) | Method of heat treatment of Al-based alloys containing Li and the product obtained by the method | |
EP0214381B1 (fr) | Alliage aluminium-lithium | |
US5116572A (en) | Aluminum-lithium alloy | |
EP0151301A1 (fr) | Alliage aluminium-lithium | |
US5160555A (en) | Aluminum-lithium alloy article | |
USRE26907E (en) | Aluminum alloys and articles made therefrom | |
US5133930A (en) | Aluminum-lithium alloy | |
EP0250656A1 (fr) | Sous-vieillissement à basse température d'alliages contenant du lithium | |
CA1267797A (fr) | Alliage d'aluminium et lithium | |
CA1280341C (fr) | Sous-vieillissement a basse temperature des alliages antifriction au lithium | |
EP0149194A2 (fr) | Alliages aluminium-lithium | |
CA1267798A (fr) | Alliage d'aluminium et lithium (4) | |
CA1135537A (fr) | Alliage a base d'aluminium | |
US3510295A (en) | Titanium base alloy |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Designated state(s): DE FR GB IT NL |
|
PUAL | Search report despatched |
Free format text: ORIGINAL CODE: 0009013 |
|
AK | Designated contracting states |
Kind code of ref document: A3 Designated state(s): DE FR GB IT NL |
|
17P | Request for examination filed |
Effective date: 19870408 |
|
17Q | First examination report despatched |
Effective date: 19871126 |
|
ITF | It: translation for a ep patent filed |
Owner name: STUDIO INGG. FISCHETTI & WEBER |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): DE FR GB IT NL |
|
ET | Fr: translation filed | ||
REF | Corresponds to: |
Ref document number: 3483607 Country of ref document: DE Date of ref document: 19901220 |
|
PLBI | Opposition filed |
Free format text: ORIGINAL CODE: 0009260 |
|
26 | Opposition filed |
Opponent name: PECHINEY Effective date: 19910704 |
|
NLR1 | Nl: opposition has been filed with the epo |
Opponent name: PECHINEY. |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: CL |
|
ITTA | It: last paid annual fee | ||
PLBM | Termination of opposition procedure: date of legal effect published |
Free format text: ORIGINAL CODE: 0009276 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: OPPOSITION PROCEDURE CLOSED |
|
27C | Opposition proceedings terminated |
Effective date: 19920907 |
|
NLR2 | Nl: decision of opposition | ||
NLT2 | Nl: modifications (of names), taken from the european patent patent bulletin |
Owner name: THE BOEING COMPANY |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: IF02 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20031203 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GB Payment date: 20031217 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: FR Payment date: 20031218 Year of fee payment: 20 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: DE Payment date: 20040202 Year of fee payment: 20 |
|
REG | Reference to a national code |
Ref country code: FR Ref legal event code: D6 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: GB Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 20041219 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: NL Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION Effective date: 20041220 |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: PE20 |
|
NLV7 | Nl: ceased due to reaching the maximum lifetime of a patent |
Effective date: 20041220 |